Nanocomposite coatings obtained by electrophoretic co-deposition of poly(etheretherketone)/graphene oxide suspensions

Nanocomposite coatings were successfully prepared by electrophoretic deposition of poly(etheretherketone) (PEEK)/graphene oxide (GO) suspensions. The GO flakes developed a large-scale co-continuous morphology with the basal plane mainly aligned with the coating surface. However, the PEEK particles were also found to be wrapped by GO nanosheets when deposited on the stainless steel substrate. Both phenomena, the co-continuous morphology and the wrapping effect, were dependent on the initial GO content in the suspension and influenced the final morphological characteristics of the thermally treated coatings. The PEEK matrix developed a dendritic morphology during its cooling from the molten state because of transcrystallinity that was induced by the incorporation of GO. The preparation of suspensions involved tip ultrasonication (TS) to deagglomerate, disperse, and mill the PEEK particles. A detailed study of the microstructure revealed that TS tended not only to reduce PEEK particle size, but also to promote an elongated shape, favourable for the nanocomposite coatings.


Introduction
Poly(oxy-1,4-phenyleneoxy-1,4-phenylenecarbonyl-1,4-phenylene) or poly(etheretherketone) (PEEK) is a high-performance and semicrystalline thermoplastic polymer in the polyaryletherketone family, which exhibits outstanding properties such as chemical, tribological, hard radiation and creep resistance as well as high strength and temperature stability, biocompatibility, low flammability without the necessity of flame-retardant additives, and low smoke emission [1][2][3][4][5]. As a result of its properties, PEEK finds a broad range of applications, ranging from medicine to aerospace and nuclear industry [5]. Particularly in the case of coating applications, PEEK-based coatings systems possess good adhesion to metallic substrates, and at the same time, they enhance the substrate resistance against wear and corrosion [6]. Electrophoretic deposition (EPD) is an effective processing method for coating deposition on a variety of substrates, offering a number of advantages such as excellent mass and thickness control, relative lowcost, and large range of materials suitable to be used, including biomaterials, composites, and nanocomposites [7,8]. EPD is a two-step colloidal process that involve electrophoresis, the migration of charged particles in a liquid suspension towards an electrode by effect of an electric field, and deposition of the particles on the electrode, forming a relatively dense coating [9].
Polymer matrix composites that incorporate fillers in the nano-or micrometric scale with the aim of tailoring desired properties (including mechanical and functional properties as well as processability) are a leading area of current materials research and development [10][11][12][13]. Carbonaceous, ceramic and metallic fillers have been used to tailor the properties of PEEK-based coatings obtained by EPD to specific requirements. Nanocomposite performance depends on different factors such as dispersion, matrix-filler interactions, and, in case of flake and fibre reinforcements, alignment [10]. In this respect, EPD is useful to develop specific microstructures from multicomponent suspensions [14]; for instance, in the study of PEEK/MoS 2 coatings by electrophoretic codeposition, MoS 2 was found to align preferentially, parallel to the coating surface [15]. Similar preferential alignment of graphene oxide (GO) nanosheets has been reported in the EPD process [16][17][18][19][20][21]. Furthermore, the incorporation of GO has two main advantages: firstly, the adhesion of GO coatings on metallic substrates after thermal treatment has been attributed to the interaction between the oxygenated functional groups of GO and the metallic surface, and thereby, GO coatings have been used as the interface between PEEK and the metallic substrate to enhance the mechanical properties [21]; secondly, p-conjugated structures in graphitic materials can form strong p-p stacking interactions with the benzene ring such that found in PEEK [22,23]. Nonetheless, direct co-deposition of PEEK/GO by EPD, which should be an attractive route to nanocomposite coatings, has not been explored so far. GO possesses a two-dimensional (2D) flat monolayer formed from crystalline domains of sp 2 -hybridised carbon atoms in a hexagonal lattice, as well as amorphous/defective domains associated with a large number of sp 3 C-O bonds, incorporated in epoxide, carbonyl, carboxyl, and hydroxyl groups [24][25][26]. GO has attracted enormous interest in recent years for its outstanding properties, including Young's modulus, strength, high specific surface area, molecular barrier properties, remarkable optical properties, and excellent thermal and electrical conductivity [26]. Because of its structural characteristics and outstanding properties, GO has been implemented as filler in the development of numerous polymer matrix nanocomposite systems for several applications [27][28][29][30][31].
In this work, nanocomposite coatings are obtained by EPD from PEEK/GO suspensions and subsequent thermal treatment. PEEK/GO suspensions are prepared in two stages: (1) TS of PEEK particles is explored as a means to optimise their shape, size, and aspect ratio, by varying the applied oscillation amplitude; (2) GO is incorporated to obtain the PEEK/GO suspensions. The micromorphology and microstructure of the resulting PEEK/GO coatings are analysed before and after the thermal treatment.
The results indicate that GO has an important role in the micromorphology of the coatings, as GO nanosheets develop a large-scale co-continuous morphology characterised by the basal plane of the nanosheets mainly aligned with the coating surface, and the wrapping of PEEK particles by GO nanosheets. Moreover, incorporation of GO promotes the transcrystallinity of PEEK after melting. temperature, T g , 143°C, and melting temperature, T m , 343°C) recommended as coating of ferrous and non-ferrous metals was acquired from Victrex PCL, UK. Single-layer graphene oxide (flake size 0.5-2.0 lm, thickness 0.6-1.2 nm, and single-layer ratio [ 80%) dispersed in deionised water, concentration of 10 mgÁmL -1 , was purchased from ACS Materials, USA. The suspension medium components, ethanol denatured with about 1% methyl ethyl ketone for analysis, and isopropanol, 99.9% purity, were supplied by EMSURE Ò and Sigma-Aldrich, respectively. Stainless steel 316 L foil (Thyssenkrupp, Germany) was used as work and counter electrodes during EPD, dimensions 15 mm 9 2 mm. Physical properties and chemical composition of stainless steel 316 L are listed in Table 1 [54]. VICTREX TM PEEK VICOTE TM 704, graphene oxide, and stainless steel 316 L are hereafter referred as PEEK, GO, and stainless steel, respectively.

Methods
The process to co-deposit PEEK/GO composite coatings introduced in this work is schematised in Fig. 1. A two-stage processing method was developed in order to prepare and optimise the multicomponent suspensions for EPD (Fig. 1a, b). Firstly, PEEK suspensions were obtained by adding the polymer powder, 3 wt%, into 40 mL of a co-solvent formed by ethanol and isopropanol, 95 and 5 vol%, respectively. PEEK particles were deagglomerated, dispersed, and milled using a 20 kHz Digital Sonifier Ò S250D disruptor (BRANSON Ultrasonic Corporation, USA) equipped with a tapered and 4.7-mmdiameter titanium microtip (Fig. 1a). TS parameters considered were pulse mode, 0.5 s ''on'' followed by 2.1 s ''off'', and effective TS time of 6 min at constant amplitude. Amplitudes values of 30 and 60% were selected to determine the effect of TS on the PEEK particle size. The microtip was submerged into the PEEK suspension until the microtip edge was 1 cm above the bottom of the 50-mL glass beaker. During TS, PEEK suspensions were cooled down to an ice bath, and their temperature was monitored in real time, at a sample rate of 4 S/s, with a type K thermocouple (RS Components GmbH, Germany) connected to a single-channel thermocouple module USB-TC01 (National Instruments, UK), and logged every second. PEEK suspension temperature remained below 20°C in all cases. The acoustic energy delivered to the ethanol/isopropanol medium was estimated following the calorimetric method [55]; more details can be found in the Supporting Information. Delivered acoustic power values of 1.5 W and 3.8 W for 30% and 60% amplitude, respectively, were obtained by applying the following equation: where P is the delivered acoustic power (W), T corresponds to the temperature (K), t represents the time (s), and M (g) and C p (JÁg -1 K -1 ) are the mass of the liquid and specific heat of liquid, respectively. By plotting the temperature against time ( Fig. S1-Supplementary Information), the value of d/dt(T) was estimated considering the linear regression slope. The C p value was proportional to the ethanol/isopropanol mixture ratio, ethanol 95 vol% and isopropanol 5 vol%, C p being 2.36 JÁg -1 ÁK -1 for ethanol and 2.57 JÁg -1 ÁK -1 for isopropanol [56,57].
In the second stage, sonicated PEEK and as-delivered GO suspensions were blended at three different compositions (Fig. 1b, c). The concentration of the starting PEEK suspension was kept constant, and a different volume of GO suspension was added for the preparation of each blend. The GO suspension was carefully transferred with a pipette from its original container to the previously ultrasonicated PEEK suspension and magnetically stirred on a stirring hotplate (VMS-C7 Advanced VWR TM , USA) for 24 h at 250 rpm and ambient temperature. Blends at compositions of 0.5, 1.0 and 3.0 wt% GO relative to the PEEK mass were prepared adding, respectively, 0.5, 1.0, and 3.0 mL of GO suspension (1 wt%) to 40 mL of PEEK suspensions (3 wt%). Table 2 summarises the characteristics of the suspensions prepared and their nomenclature used hereafter to identify them.
EPD experiments were carried out at constant voltage and ambient temperature (Fig. 1d). The microstructural homogeneity and thickness of the coating heavily influenced by voltage. Thereby, in order to observe the effect of voltage on co-deposited PEEK/GO coatings, 10 and 30 V were considered for EPD and adjusted using a DC power supply EL752M multimode (Thurlby Thandar Instruments, UK). Stainless steel electrode plates of dimensions (30 mm 9 15 mm 9 2 mm) were mirror-polished with a P600 CarbiMetTM grinding paper (Bü hler Group, Switzerland) and cleaned for 30 min in an ethanolic medium by means of a SONOREX super RK 100 (BANDELIN electronic GmbH & Co. KG, Germany) before EPD to improve the adhesion of the coating to the stainless steel substrate. Two stainless steel electrodes were submerged into the PEEK or PEEK/GO suspension at the centre of a borosilicate beaker in a parallel plate arrangement (10 mm distance between plates) to achieve a uniform electric field between the plates. Deposition times from 1 to 5 min were considered because some PEEK particles formed a thin layer at the bottom of the beaker after 8 min due to sedimentation; nevertheless, low turbidity was achieved after 40 min, and the suspensions were suitable for EPD. After deposition, the coated electrode plates were carefully extracted from the suspension to prevent damage to the deposited  layer, Fig. 1e. The EPD coatings were labelled with reference to the suspension used for their preparation, see Table 2.
Prior to thermal treatment, Fig. 1f, samples were dried at 150°C for 3 h, according to the recommendations given by the manufacturer, in a muffle furnace P330 (Nabertherm GmbH, Germany). Thermal treatment was carried out in air applying the following thermal cycle: heating from room temperature to 380°C at a rate of 10°CÁmin -1 , followed by an isothermal step at 380°C for 5 min; finally, cooling from 380°C to room temperature at a rate of 2°CÁmin -1 . Instruments described previously to monitor the temperature during sonication were also used to monitor the temperature in real time during the drying and thermal treatment stages, and the temperature values were logged every minute in both cases. A representative sample after drying and thermal treatment is presented in Fig. 1g. Table 2 lists the nomenclature followed to designate the thermally treated coatings; in all cases, the nomenclature is associated with the suspension from which the coating was obtained.

Scanning electron microscopy
Scanning electron microscopy (SEM) images were taken on a field-emission microscope ZEISS Gemini SEM 450 (ZEISS, Germany) equipped with an in-lens secondary electron detector. Graphene oxide is highly electron transparent as a result of its 2D structure and low atomic number, and it can be transparent when high accelerating voltages are set because the incident electrons pass more easily thorough the GO nanosheets [58]. Hence, an accelerating voltage of 1 kV and probe current of 10 nA were selected to favour the observation of GO nanosheet details and to ensure comparability between the materials prepared. SEM images were taken for raw PEEK particles and PEEK/GO composite coatings; the latter ones were examined before and after the thermal treatment. Before SEM analysis, samples were dried at 60°C for 24 h in a drying oven with natural convection (DL 115 DRY-line Ò , VWR International BVBA, Belgium) and subsequently coated with Au into a sputter coater (Q150T S Plus, Quorum, UK) to prevent sample charging.
With the aim of determining the TS effect on the PEEK particle characteristics, volumes of 50 lL of PEEK suspensions tip-ultrasonicated at different amplitudes were gently deposited on aluminium conductive tape with a micro-pipette to determine the effect of TS on the characteristics of PEEK particles. A detailed analysis of the SEM micrographs of the deposited PEEK particles was performed by means of ImageJ software (version 1.52a) and Wolfram Mathematica Ò (version 8.0.0.0). For every single particle, the contour was traced, and the minor and major particle axes were determined using ImageJ software. Representative results were ensured by considering over 400 particles for SEM micrograph. In addition, bivariate probability density distributions (BPDDs) were obtained. BPDD comprised a total of 1600 subregions, 40 horizontal subintervals, and 40 vertical ones. Kernel density estimation (KDE) was calculated considering Silverman's rule and Gaussian kernel [59] by implementing Wolfram Mathematica Ò .

Fourier-transform infrared spectroscopy
Infrared spectra were recorded in the wavenumber interval from 4000 to 600 cm -1 , 40 scans, 4 cm -1 resolution and 4.3 cm aperture, by using an IRTracer-100 (Shimadzu Corp., Japan) Fourier transform infrared (FTIR) spectrometer equipped with a highenergy ceramic light source and a deuterated L-alanine triglycine sulphate (DLATGS) detector. FTIR spectrometer was coupled to a single reflection attenuated total reflectance (ATR) system (Quest, Specac Ltd., UK), 45°nominal angle of incidence, equipped with a diamond prism. Samples were placed on the diamond prism and pressed to its surface by mean of compression rod. Spectrum software (version 10.02.00.0041) was used in the analysis of the ATR-FTIR spectra.
X-ray diffraction X-ray diffraction (XRD) characterisation of PEEK and PEEK/GO coatings was carried out at room temperature by using a Rigaku Miniflex TM 600 (Rigaku, Japan) X-ray diffractometer provided with a Cu-Ka radiation (k = 1.5406 Å ) X-ray source and scintillation counter (Kb filter) detector. The instrument was operated at 40 kV and 15 mA. XRD patterns were recorded from the specimen surface in the angular J Mater Sci (2020) 55:8881-8899 range (2h) from 5 to 40°, considering a resolution of 0.01°and speed scanning of 0.5°Ámin -1 .

Results and discussion
Effect of tip ultrasonication on the PEEK particles Acoustic cavitation produced during TS promotes highly intense local conditions characterised by short-lifetime hot spots whose temperature rises to 5000°C, reaching pressure values of around 1000 atm, and cooling rates of 10 10 KÁs -1 [60]. Even though propagation of ultrasonic waves in liquids is generally considered as an adiabatic process because of the rapid pressure variation [61], the highly intense local conditions can cause ceramic, metallic, carbonaceous, and polymeric particles to experience, according to their nature, changes of their molecular weight, chemical and crystalline structure, and morphology [32,33,[61][62][63][64][65][66][67]. Hence, the first step was to determine the effects of TS on PEEK particles.
In principle, FTIR spectroscopy can be used to monitor variations in the molecular weight, and chemical and crystalline structure. FTIR spectra of neat PEEK particles is presented in Fig. 2a. The thermal degradation mechanism of PEEK involves random scission of ketone and ether linkages [68][69][70], leading to the disappearance of characteristic PEEK bands in mid-infrared (MIR) at 1652 cm -1 m (C=O) , 1225 cm -1 m (u-O-u) , 1010 cm -1 m (C-O-C) or m (C-O) , and 927 cm -1 m sym(u-(C=O)-u) , and, to the development of a band at 1709 cm -1 related to an aldehyde group, which is well defined even at weight loss values as low as 5% [71]. In contrast to thermal degradation, the ultrasonic degradation of polymers in solution is coupled to a non-stochastic mechano-chemical shear; long polymer chains are, therefore, degraded much more rapidly than small ones, resulting in average molecular weight (M w ) reduction at earlier stages [61]. In the present experiments, PEEK particles were insoluble in the ethanol/isopropanol medium, and the differences in the spectra for the neat PEEK and processed polymer after TS at constant amplitude values of 30 and 60% were modest (Fig. 2a). Moreover, there was no evidence of new bands associated with aldehyde or other groups as possible result of a thermal degradation mechanism; however, there was a slight intensity reduction and shift of PEEK characteristic bands after TS (see inset in Fig. 2a), with increasing amplitude. This behaviour can be attributed to M w reduction of the PEEK particles, and, in last instance, to a small contribution from ultrasonic degradation of PEEK. Similar results have been found in ultrasonication of chitosan nanoparticles [66].
Crystallinity plays an important role in semicrystalline polymers, not only because it affects their final properties, but also for the EPD process itself. Amorphous polymer chains extending out of the particle surface make a major contribution to the suspension stability [48]. The behaviour of insoluble polymer particles in suspensions is similar to that of solid particles such as metals and ceramics with adsorbed polymers on their surfaces [72][73][74]. TS is known to modify material crystallinity in some cases [33], but the effects on PEEK are not yet established. FTIR provides an alternative to estimate the degree of crystallinity; in case of PEEK, it is through the MIR bands at 1305 cm -1 m (C=O) , 1280 cm -1 m (C=O) , 966 cm -1 x (CH) , and 952 cm -1 x (CH) [75][76][77][78][79]. By using these bands, Chalmers et al. [75] and Cebe et al. [77] established calibration curves to quantify the degree of crystallinity of PEEK from FTIR measurements. In this work, the calibration curve for the C-H wagging mode reported by Cebe et al. [77] is applied, as it uses the band area rather than intensity ratio and was cross-checked against a range of techniques to determine the degree of crystallinity. According to the FTIR measurements and the selected calibration curve, no significant variations in the degree of crystallinity of PEEK were detected under the TS experimental conditions ( Table 3). The degree of crystallinity was also estimated from XRD measurements: Fig. 2b shows XRD patterns of the pristine PEEK powder before and after tip sonication considering amplitudes of 30 and 60%. PEEK has an orthorhombic unit cell where the polymer backbones are aligned with the c-axis, giving rise to four main peaks in the XRD diffractogram at 2h values of approximately 19°, 21°, 23°, and 29°, assigned to the (110), (111), (200), and (211) crystalline planes, respectively [80][81][82][83]. The degree of crystallinity for pristine and tip sonicated PEEK powders was estimated from XRD measurements according to the procedure reported in the literature [81,83]; the values are summarised in Table 3. A comparison between the degree of crystallinity measured by XRD and deduced from FTIR calibration curve [77] shows a good correlation between the two methods and suggests that the effect of TS on the crystallinity of PEEK is minor and can be neglected. In addition to the particle's structure, its overall morphology is a key factor in the processing and properties of composites and nanocomposites. During TS, polymer particles may change morphology, depending on both process parameters (power, amplitude, suspension concentration, suspension volume, and microtip diameter/length immersed) and the characteristics of the particles (initial size, and their chemical and physical characteristics). TS is commonly associated with reduction of particle size; however, under some conditions, TS increases the polymer particle size; for example, an increase in particle size has been observed in TS of poly(methyl methacrylate) particles, where the authors attributed the behaviour to the fusion of the beads in dumbbelllike structures [65]. Light-scattering (LS) techniques have been used to estimate PEEK particle size after TS; nevertheless, agglomeration and precipitation of the particles cause fluctuations in the measurements [37,39]. Furthermore, the effects of TS on PEEK particle shape have not been reported; thus, a detailed SEM study was performed here. A large number of SEM images (up to 10 images, more than 400 particles analysed in each image) was obtained (typical example in Fig. 3a) and analysed quantitatively to obtain a BPDD which offers valuable information about how the variables interact or are correlated with each other (Fig. 3b). The initial PEEK particles are defined by major and minor particle size values B 40 lm. Tick marks situated close to the BPDD axes show the locations of the individual observations. The diagonal line indicates the location of equiaxed particles, with an aspect ratio of 1. Rounded particles (e.g. particle numbered 1 in Fig. 3a) appear near the line in Fig. 3b, and elongated particles (e.g. particle number 2 in Fig. 3a) lie further away. There are relatively fewer larger particles (major axis over * 20 lm), but those that are present tend to be more elongated (Fig. 3b).
Despite the fact that BPDD provides valuable information, noise in the measurement process and  The considered MIR bands correspond to x(CH) modes subinterval size can influence the result; for example, the probability that an observation lies in a subinterval depends on the subinterval size selected. By contrast, the use of KDE reduces these effects, allowing a fundamental data smoothing where inferences about the population are made [84]. KDE values derived from the individual observations are shown in Fig. 3c. The representation of the experimental observations in terms of KDE shows a distinct broad peak, indicated by the arrow, whose coordinates are related to the estimated particle sizes with the highest probability. This peak is centred at 13 lm (major size) and 9 lm (minor size) values, implying an average aspect ratio around 1.4. An archetypal PEEK particle with the characteristics described above is indicated in Fig. 3a as number 3. After TS, both BPDD and KDE show a significant reduction in modal particle size, as well as an increase in particles smaller than 20 lm (Fig. 3). KDE (Fig. 3i) highlights that particles below 5 lm are the dominant ones after the higher amplitude (60%) treatment. At 30% amplitude (Fig. 3f), the distribution is bimodal, and the larger peak shifts to lower size values in respect to the original particle distribution. The shifts of distribution were observed to be correlated with the amplitude (Fig. 3f, i); nevertheless, the particle size was reduced by only 30% though the amplitude was doubled. This behaviour is consistent with that observed in polymers and other materials, where the rate decreases with particle size as consequence of energy lost in particle motion, compression, flexing, and other mechanisms rather than fragmentation [50]. Although the LS measurements in the case of PEEK particles are time dependent because of particle agglomeration and precipitation, the particle sizes determined by SEM are consistent with the range of values determined by means of LS of a few to tens of microns [37,39]. Interestingly, TS generates more elongated PEEK particles, with the aspect ratio increasing from 1.4 for the original powder to 1.75 to 2.5 when the amplitude is increased from 30 to 60%, respectively. Table 4 lists additional statistical parameters for neat PEEK and tip-ultrasonicated PEEK particles.
After TS, the PEEK particle dimensions are closer to the GO flake size, 0.5-2.0 lm, and have a more elongated shape, which may be an advantage in their interaction with the 2D nanosheets. Although there were only minimal changes in PEEK molecular weight and crystallinity, extended TS can be undesirable. High amplitudes increase the unavoidable erosion of the microtip, introducing impurities and contaminating the suspension. Therefore, a 30% constant amplitude was selected for subsequent processing of the PEEK powder.

PEEK/GO coatings
The suspensions of PEEK particles and GO were mixed and then deposited by EPD onto stainless steel substrates, to form high-quality, uniform coatings. SEM micrographs show that the GO nanosheets are homogeneously distributed across the coating (Fig. 4) and also suggest two characteristic modes of interaction between the two phases after EPD and subsequent drying process: nanosheets deposited on the top or trapped in between the PEEK particles (Fig. 4a,  b); and nanosheets wrapping the particles (Fig. 4c). Most importantly, SEM micrographs indicate that GO nanosheets form a co-continuous structure (Fig. 4df). The large GO nanosheet structures have dimensions exceeding the flake size indicated by the manufacturer, 0.5-2.0 lm, suggesting an assembly process during the EPD. GO continuous morphologies [85] and GO alignment have been reported [86]. Nevertheless, in the present conditions, though it is plausible that the position of the GO nanosheets could differ from the horizontal position, it is remarkable that the GO nanosheets basal plane is predominantly aligned with the nanocomposite coating surface, forming structures whose dimensions are larger than several thousands of lm. SEM at increasing magnification shows the assembly process in more detail (indicated by the arrows in Fig. 4d-f).
Alignment of GO nanosheets, as result of EPD, has been discussed in the literature [17][18][19][20]. One explanation is that the basal plane will align to the direction of the applied electric field during EPD due to the anisotropic polarizability of the GO nanosheets; another possibility is that the GO aligns parallel to the substrate either due to rotation during deposition or due to capillary effects during drying. Large and aligned discontinuous GO structures were formed with 0.5 wt% GO loading in suspension (Fig. 5a, d), but as the GO content increased to 1.0 wt%, the cocontinuous morphology appeared (Fig. 5b, e), becoming more prominent at 3.0 wt% (Fig. 5c, f).
Regarding PEEK particle size and aspect ratio after EPD, it is not straightforward to quantify these parameters from SEM micrographs. Even by increasing the accelerating voltage from 1 to 10 kV (Fig. 6) with the aim of varying the transparency of the GO nanosheets to the electron beam [58,87], allowing PEEK particles to be visualised underneath, GO flakes are seen to cover the particles, specially small particles. Nonetheless, the majority of the observable deposited PEEK particles have a size below 10 lm, exhibiting elongated shape of low aspect ratio (Fig. 5d-f), although there was a considerable population of particles (after TS) with major size ranging between 10 and 20 lm after TS (Fig. 3d-f). This effect is likely associated with the sedimentation of large PEEK particles during EPD. Composition, particle size and shape, and size distribution are key factors dictating the success of EPD [88,89], confirming that TS is an effective strategy to prepare suitable suspensions containing PEEK powders and GO for EPD. Macroscopically, PEEK/GO nanocomposite coatings deposited at 30 V were, in general, more  uniform and thicker than those deposited at 10 V. Nevertheless, there was a significant edge effect when deposition time was extended over 4 min (Fig. 7), especially when the GO concentration increased in the suspension, leading to crack formation along the substrate edges. Therefore, samples prepared by EPD at 30 V and 3 min were selected for further analysis.
Electrophoretic deposition of PEEK requires a postsintering process in order to densify the coating, as well as to enhance the adhesion to the stainless steel substrate [40-42, 44, 45, 49]. Digital images of the dried and thermally treated PEEK/GO coatings (Fig. 8) show coherent coatings. PEEK/0.5GO_TT and PEEK/1.0GO_TT were uniform in the centre of the sample, Fig. 8a, b, but a darker area was visible close to the substrate edges in both coatings. In contrast, PEEK/3.0GO_TT was relatively uniform. These macroscopic features may be related to the wettability and viscosity of the melted PEEK, being both phenomena, wettability and viscosity, dependent on the heat-treatment temperature [90]. Moreover, GO can substantially increase the viscosity in polymers above the rheological percolation threshold [91], and, in PEEK/GO composites, the viscosity could be increased one order of magnitude with respect to neat PEEK even at GO concentrations lower than 5% [92]. This suggests that the nanosheets impede the free spreading of the melted PEEK over the surface, specially, at the edges (Fig. 8), where it is likely that more GO is deposited due to field enhanced deposition (Fig. 7).
The uniform central region of the consolidated PEEK/GO_TT coatings (Fig. 8) was studied by SEM, XRD, and FTIR to explore the effects of GO. Increasing GO content creates a rougher, more irregular surface (Fig. 9a-c). These irregularities can be attributed to the GO nanosheet structure. PEEK particles wrapped by GO nanosheets after EPD (Fig. 4c) may not be able to integrate into the continuous film during melting. Comparison of the SEM micrographs of Fig. 5d-f with those in Fig. 9a-c shows that the size and distribution of the particles before thermal treatment correspond with the observed irregularities. Furthermore, the texture of the co-continuous GO phase may be also manifested in the coating surface (compare Fig. 5). In addition to the micron-scale texture, a finer dendritic morphology with preferential orientation appears on all samples in the polymer-rich regions, which decreases at higher values of GO wt%; meanwhile, the roughness increases ( Fig. 9d-f). This dendritic morphology was also found in neat PEEK coatings after drying and thermal treatment (PEEK_TT) at the boundaries of the coating (Fig. 10).
Transcrystallinity or surface crystallisation is a condition where nucleation and crystalline growth are affected by an existing surface; as a result, spherulites originate at the surface and grow normal to it. Transcrystallinity has been reported for PEEK on different substrates [76,80,93], and more recently on GO [94]. In PEEK/GO composites obtained by injection moulding, a PEEK dendritic morphology similar to that shown in Fig. 10 was observed growing with preferential orientation on a GO flake and it was related to changes in the ratio of the (110) to (200) peak intensities of the bulk XRD patterns [94].
Analogously, the XRD pattern for the PEEK/ 3.0GO_TT coating (Fig. 11) showed a decrease in the ratio of the (110) to (200) peak intensities in comparison with those of pure PEEK and PEEK_TT, indicating an important increase in the crystalline phase as a result of the thermal treatment in both PEEK_TT and PEEK/GO_TT coatings. The degree of crystallisation for PEEK_TT and PEEK/3.0GO_TT coatings is summarised in Table 5. Thermal treatment tends to increase the degree of crystallisation of pure PEEK (Tables 3, 5) [77,81,83]; nevertheless, graphene appears to have a nucleating effect for the crystallisation of PEEK from the melt and to affect the crystalline growth as well [94,95]. In the case of PEEK/ 3.0GO_TT coating, the degree of crystallinity appears to be reduced by the co-continuous GO structure within the PEEK composite (Table 5). A similar effect has been recently reported in a non-isothermal  crystallisation study of PEEK/graphene nanoplate composites by synchrotron X-ray diffraction [95].
On the other hand, location and chemical structure of the surrounding polymer, in addition to time and temperature, have been observed to affect the in-situ reduction of GO in polymer matrix composites [96,97]. In this respect, the FTIR spectrum of neat GO after thermal treatment, GO_TT, is shown in Fig. 12, and it is compared with those of PEEK_TT and PEEK/3.0GO_TT. In the inset of Fig. 12, the contribution of GO_TT and PEEK_TT to the PEEK/ 3.0GO_TT spectrum is presented. During thermal reduction of GO, the restoration of the aromatic rings gives rise to the band at 1570 cm -1 , indicated in the inset of Fig. 12, which is associated with C = C stretching vibration of the sp 2 hybridised carbon atoms [97]. Additionally, the thermal treatment also induced changes in those bands associated with crystallinity [75][76][77][78][79]. However, there was no sign of the aldehyde band at 1709 cm -1 which is associated with the onset of thermal degradation of PEEK [71], thus confirming an adequate thermal treatment adopted in this work. The degree of crystallisation of PEEK_TT estimated by considering the calibration curve [77] agreed with the XRD measurements (Table 5).
Another important characteristic is that the morphology of the PEEK/3.0GO_EPD coating developed at 10 V and 1-min deposition time (Fig. 4f) and that of the coating obtained at 30 V and 3 min deposition  time were similar (Fig. 5f). Thereby, it is reasonable to conceive the characteristics of the coating morphology across the cross section as being similar to those on the coating surfaces. This conception of the coating morphology is supported by SEM images of the coating cross sections (Fig. 13), for PEEK/3.0GO_TT prepared at deposition time of 3 min, highlighting the consistent microstructure throughout the EPD film. The texture observed on the upper surface of the films is due to the presence of the wrapped PEEK particles (Fig. 13a, b). In addition, similar to the surface morphology (Fig. 9a-f), both wrapped PEEK particles and PEEK dendrites are observed (Fig. 13c,  d).

Conclusions
Intense tip sonication of PEEK particle suspensions reduced the particle size and increased the aspect ratio without significantly affecting PEEK chemical structure and degree of crystallinity. The reduced size was considered an advantage for the preparation of PEEK/GO coatings by EPD.
The resulting PEEK suspensions were successfully mixed with GO suspensions and used for the preparation of composite coatings by electrophoretic co-deposition. The resulting microstructure displayed an intimate interaction between the polymer and GO nanosheets homogeneously across and throughout the coatings. The two phases formed a cocontinuous architecture, built around an aligned network of GO, particularly favoured by high GO concentrations. The presence of GO created a texture in the consolidated (heat-treated) polymer films, Figure 11 XRD patterns of neat PEEK, PEEK_TT and PEEK/ 3.0GO_TT. The considered MIR bands correspond to x(CH) modes preserving some characteristics of the original PEEK particles, the wrapping effect, as well as nucleating a high degree of PEEK matrix and inducing transcrystallinity. These PEEK/GO nanocomposite coatings obtained by EPD may have promising properties given their unique morphological characteristics. The continuous network of GO nanosheets should provide electrical and thermal conductivity, once the GO is reduced, for example during the heating treatment used to consolidate the polymer. It may also contribute to achieve superior mechanical properties, regarding the elastic modulus, hardness, and other important coating characteristics such as impact and abrasion resistance. The presence of carbon nanofillers in PEEK is known to improve properties both through direct reinforcement and improvement in matrix microstructure [98], particularly crystallinity, as observed here. In this respect, the emphasis of our future work will be the characterisation of the coating physical properties and the relationship of the properties with the micromorphology observed. The deposition of PEEK/GO coatings by EPD is attractive, representing a simple and efficient technology to create useful nanocomposites on a wide range of substrates, including curved surfaces. Such systems may be relevant to applications in industrial and food processing, and in the textile, medical, oil, and gas sectors.

Acknowledgements
Open Access funding provided by Projekt DEAL. Eduin I. González-Castillo gratefully acknowledges the National Council of Science and Technology (CONACYT, Mexico) for the postdoctoral scholarship given (Reference: 239274) to carry out his project proposal in Germany.

Compliance with ethical standards
Conflict of interest There is no conflict of interest.
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